EP1114197A4 - Modified nickel-chromium-aluminum-iron alloy - Google Patents
Modified nickel-chromium-aluminum-iron alloyInfo
- Publication number
- EP1114197A4 EP1114197A4 EP99945036A EP99945036A EP1114197A4 EP 1114197 A4 EP1114197 A4 EP 1114197A4 EP 99945036 A EP99945036 A EP 99945036A EP 99945036 A EP99945036 A EP 99945036A EP 1114197 A4 EP1114197 A4 EP 1114197A4
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- aluminum
- matrix
- nickel
- healing
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000640 Fe alloy Inorganic materials 0.000 title description 6
- -1 Modified nickel-chromium-aluminum-iron Chemical class 0.000 title description 6
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 160
- 239000000956 alloy Substances 0.000 claims abstract description 160
- 239000011159 matrix material Substances 0.000 claims abstract description 45
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 44
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 41
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 34
- 239000011651 chromium Substances 0.000 claims abstract description 25
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 24
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 24
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 20
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims abstract description 20
- 230000003647 oxidation Effects 0.000 claims abstract description 19
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 19
- 229910052742 iron Inorganic materials 0.000 claims abstract description 18
- 230000001590 oxidative effect Effects 0.000 claims abstract description 18
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 16
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 16
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 16
- 239000011575 calcium Substances 0.000 claims abstract description 16
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 15
- 239000001301 oxygen Substances 0.000 claims abstract description 15
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 10
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 claims abstract description 9
- 230000002411 adverse Effects 0.000 claims abstract description 9
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 239000011593 sulfur Substances 0.000 claims abstract description 9
- 230000006911 nucleation Effects 0.000 claims abstract description 8
- 238000010899 nucleation Methods 0.000 claims abstract description 8
- 238000009827 uniform distribution Methods 0.000 claims abstract description 8
- 239000000203 mixture Substances 0.000 claims description 29
- 238000010438 heat treatment Methods 0.000 claims description 15
- 230000015572 biosynthetic process Effects 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- 230000002401 inhibitory effect Effects 0.000 claims description 7
- 238000000034 method Methods 0.000 claims description 7
- 230000035876 healing Effects 0.000 claims description 5
- 230000000087 stabilizing effect Effects 0.000 claims description 5
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 230000004584 weight gain Effects 0.000 claims description 4
- 235000019786 weight gain Nutrition 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 239000005864 Sulphur Substances 0.000 claims 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims 2
- 229910052796 boron Inorganic materials 0.000 claims 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims 1
- 239000000654 additive Substances 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 claims 1
- 238000007792 addition Methods 0.000 abstract description 11
- 238000005382 thermal cycling Methods 0.000 abstract description 6
- 239000006104 solid solution Substances 0.000 abstract description 4
- 230000014759 maintenance of location Effects 0.000 abstract description 2
- 239000000243 solution Substances 0.000 description 35
- 239000000463 material Substances 0.000 description 26
- 230000032683 aging Effects 0.000 description 19
- 238000012360 testing method Methods 0.000 description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 11
- 239000010410 layer Substances 0.000 description 10
- 230000000694 effects Effects 0.000 description 8
- 239000002245 particle Substances 0.000 description 8
- 239000003570 air Substances 0.000 description 6
- 230000008859 change Effects 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000004458 analytical method Methods 0.000 description 5
- 239000000155 melt Substances 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- 239000012798 spherical particle Substances 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 238000004626 scanning electron microscopy Methods 0.000 description 4
- 229910000990 Ni alloy Inorganic materials 0.000 description 3
- 229910018487 Ni—Cr Inorganic materials 0.000 description 3
- BIJOYKCOMBZXAE-UHFFFAOYSA-N chromium iron nickel Chemical compound [Cr].[Fe].[Ni] BIJOYKCOMBZXAE-UHFFFAOYSA-N 0.000 description 3
- VNNRSPGTAMTISX-UHFFFAOYSA-N chromium nickel Chemical compound [Cr].[Ni] VNNRSPGTAMTISX-UHFFFAOYSA-N 0.000 description 3
- 230000001351 cycling effect Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 230000007246 mechanism Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000001000 micrograph Methods 0.000 description 3
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- 238000004901 spalling Methods 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 125000003821 2-(trimethylsilyl)ethoxymethyl group Chemical group [H]C([H])([H])[Si](C([H])([H])[H])(C([H])([H])[H])C([H])([H])C(OC([H])([H])[*])([H])[H] 0.000 description 2
- 208000032538 Depersonalisation Diseases 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 229910000623 nickel–chromium alloy Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 239000011241 protective layer Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 235000012431 wafers Nutrition 0.000 description 2
- RZVAJINKPMORJF-UHFFFAOYSA-N Acetaminophen Chemical compound CC(=O)NC1=CC=C(O)C=C1 RZVAJINKPMORJF-UHFFFAOYSA-N 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910001005 Ni3Al Inorganic materials 0.000 description 1
- 230000001464 adherent effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical group [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- 239000012080 ambient air Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000000788 chromium alloy Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005485 electric heating Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 230000006870 function Effects 0.000 description 1
- 229910044991 metal oxide Inorganic materials 0.000 description 1
- 150000004706 metal oxides Chemical class 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000002028 premature Effects 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000009993 protective function Effects 0.000 description 1
- 239000005297 pyrex Substances 0.000 description 1
- 238000011002 quantification Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000009257 reactivity Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000007655 standard test method Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01C—RESISTORS
- H01C1/00—Details
- H01C1/02—Housing; Enclosing; Embedding; Filling the housing or enclosure
- H01C1/028—Housing; Enclosing; Embedding; Filling the housing or enclosure the resistive element being embedded in insulation with outer enclosing sheath
-
- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
- H05B3/00—Ohmic-resistance heating
- H05B3/10—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor
-
- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
- H05B3/00—Ohmic-resistance heating
- H05B3/10—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor
- H05B3/12—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor characterised by the composition or nature of the conductive material
Definitions
- the present invention relates to nickel-chromium-aluminum-iron
- Nickel-chromium-iron alloys are used primarily for their oxidation
- Such alloys may be used, for example,
- thermocouples as sheathing for electric heating elements and thermocouples.
- resistance alloys used for generation of heat are referred to as resistance
- resistance heating elements are designed for
- Such heaters are constructed to provide more effective
- U.S. Patent No. 2,515,185 relates to nickel alloys, and more
- the invention relates to an oxidation-resistant alloy for use in a high
- the alloy is relatively readily
- the alloy has a nickel-based matrix
- FIGURE 1 depicts the results of an accelerated life test of several
- FIGURE 2 depicts the steps for processing the alloy of the present
- the alloy of the present invention is an oxidation-resistant alloy for
- VHN Vickers hardness
- the alloy has a nickel-
- based matrix including, by weight, about 19-23 chromium and about 3-6
- the alloy also includes about 0.005-0.05, and preferably about
- the aluminum in the alloy may combine with oxygen in the environment to form a self-healing means for
- thermodynamically stable oxide layer if it becomes damaged or spalls in use.
- oxide layer protects the alloy from the oxidizing atmosphere.
- Aluminum is added for oxidation resistance. Its favorable
- Table 3 illustrates the VHN of the as-cast material before solution treatment:
- Table 6 details the hardness results obtained for each of the samples following the aging treatment (5 hours at 650 °C and then air-cooled). Recall that after the initial solution treatment the samples followed by a "1 " were air-cooled and the samples followed by a "2" were water quenched. The results show very little change in hardness from the as-cast condition. There also appears to be no correlation between the cooling rate after solution treatment and the hardness after aging.
- Table 8 details the hardness results obtained for each of the samples in the hot worked condition prior to the solution treatment. Note the significantly higher hardness of the samples from heat 22270, presumably due to the fact that those samples had not been annealed.
- Table 10 details the hardness results obtained for each of these samples.
- the water-quench produces material that is markedly softer than the air- cooled material. This indicates the probable formation of a second phase in the alloy at slower cooling rates. Again note that the VHN value for 22270-2 is now comparable with the other samples.
- Table 11 details the hardness results obtained for each of the samples following the aging treatment (5 hours at 650 °C and then air-cooled). Recall that after the initial solution treatment the samples followed by a " 1 " were air-cooled and the samples followed by a "2" were water quenched. The results show very little change in hardness from the initial hot-worked condition (except in the case of 22270, which had not been annealed). There also appears to be no correlation between the cooling rate after solution treatment and the hardness after aging.
- compositions were produced by weighing up to 10 pound charges and melting them. Foundry and rolled samples were prepared. Foundry samples were analyzed for chemical composition and sectioned to prepare samples which represent the as-cast condition for study. The rolled samples were used to produce hot-work material to study the wrought condition of the compositions.
- Table 12 provides the analyzed chemistry composition for both of the heats used in the study. TABLE 12
- Table 13 details the hardness results obtained for each of the samples prior to the solution treatment.
- Table 15 details the hardness results obtained for each of these samples.
- the water-quench produces material that is markedly softer than the air- cooled material.
- Table 16 details the hardness results obtained for each of the samples following the aging treatment (5 hours at 650 °C and then air-cooled). Recall that after the initial solution treatment the samples followed by a " 1 " were air-cooled and the samples followed by a "2" were water quenched. There is a correlation between the aging treatment and hardenability in these compositions, especially in the high Al, Cr and Fe sample (X138). In all cases, the effect was strongest on samples that were water-quenched after the solutioning treatment.
- Heat X1378 (High Al, Cr, and Fe) has a VHN greater than 500 following the solution and aging treatment outlined in JP 59-85836. Only the material that was water quenched after solution treatment produced material with a VHN of at least 500.
- Alloy 22283, X1377-2 andX1378 alloys were prepared in accordance with the present invention.
- Alloy 22283 is a more preferred composition of the present invention.
- Alloy XI 377-2 has amounts of aluminum and chromium near the upper limit of the present invention.
- Alloy XI 378-2 has amounts of aluminum, chromium and iron near the upper limits of the present invention.
- the final heat treatment was a solution treatment for 2 hr. at 1200°C followed by water- quenching.
- the quenched samples were aged for 5 hr at 650°C.
- This alloy shows two distinctly different phases.
- High- magnification scanning electron microscopy (SEM) shows the two phases to be distinctly different.
- the second phase has a fairly large fraction of the microstructure.
- This alloy also shows distinct second phase, but the amount is much smaller than Alloy XI 378-2.
- Alloys 17032 and 17033 These alloys show second phase distributed throughout.
- High-magnification SEMs of alloy XI 378-2 show that the second phase has a very fine lamellar microstructure.
- a careful microhardness measurement shows that the matrix has a hardness of 288 + 21 and that the lamellar phase a value of 655 + 9.
- the larger standard deviation in the hardness of the second phase in alloy XI 377-2 may be due to nonuniformity in distribution of the spherical particles as opposed to perfectly aligned particles in the second phase of alloy X1378-2.
- a microprobe analysis in Table 20 indicates the presence of large gamma-prime particles at the grain boundaries. It is believed that the lamellar looking microstructure is also gamma prime, but was too fine for chemical analysis. It is believed that spherical particles in alloy XI 377-2 are the same as the lamellar structure in alloy 1378-2, and that they are gamma prime. Micrographs of alloys 17032 and 17033 show fairly uniform distribution of large particles rather than distinct two phase regions observed in alloys X1377-2 and X1378-2. The repeated microhardness of alloys 17032 and 17033 gave values of 700 + 14 and 705 + 9, respectively. The uniformity of the hardness in these samples suggest that the hardening phase is uniformly distributed. Higher magnification micrographs show the presence of a very fine lamellar structure in both alloys 17032 and 17033. This lamellar structure is somehow different than the very uniformly-spaced lamellar structure in alloy X1378-2.
- This composition is enriched in aluminum and is typical of gamma prime.
- the gamma prime is Ni 3 (Al, Ti, Nb, Ta). It could be (Ni Cr Fe) 3 Al.
- c This phase is rich in chromium and very low in aluminum. Its composition matches that of alpha-chromium.
- d This phase is very rich in chromium and very low in aluminum, and contains a small amount of titanium. Its composition matches that of alpha- chromium.
- the microprobe analysis in Table 20 had shown the coarse gray particles to be alpha-chromium. It is believed that the same alpha-chromium particles that are present as finely spaced lamellar caused the large hardening observed in alloys 17032 and 17033. The titanium addition in alloy 17033 did not seem to have a significant effect in modifying the microstructure.
- the nominal alloy 22283-1 did not show any features in the optical structure. Its second check of microhardness of 289+/-14 VHN is consistent essentially with a solid solution alloy.
- Alloys X1378-2 and X1377-2 consist of two phases (the matrix and the second phase). The second phase had significantly higher (655 and 540, respectively) hardness than the matrix phase (288 and 331, respectively). The second phase hardening is believed to be from very fine gamma prime.
- the gamma prime in the low iron content, alloy X1377-2 is typical of gamma prime (spherical particles) observed in nickel-based superalloys.
- the higher iron containing alloy X1378-2 contained gamma prime as the lamellar morphology; 2.
- compositions are of the solid alloy.
- Oxidation tests were conducted at 2200 °F for 80 hours and at 2300°F for 195 hours to compare oxidation resistance of the seven alloys.
- Table 22 a specific weight loss is caused by spalling of the oxide scale during cycling.
- Table 22 also shows that following an effective reduction in the sulfur content by combination with calcium and/or yttrium, the alloy may exhibit a slight weight gain through the formation of a protective scale of alumina. Desulfurized specimens tend to show a positive specific weight change throughout the duration of the life test.
- compositions are of the solid alloy.
- the inventors have observed that the advanced alloys and coatings disclosed rely on the formation and adherence of a thin and continuous aluminum oxide film to protect the base alloy from further oxidation attack at elevated temperatures.
- the alumina scale In order for the alumina scale to serve its protective function, it must remain adherent to the underlying alloy under prolonged exposure and thermal cycling conditions. It is known that segregation of indigenous sulfur to the metal-oxide interface induces premature scale spalling of the scale. This may occur through a reduction in the interfacial adhesion strength, with a resulting reduction in component lifetime.
- the inherent reactivity of yttrium requires an exceptionally high degree of control over alloy chemistry during melting/casting.
- Control of the concentration of the reactive element additions is particularly important, since retention of a minimum amount in solution in cast alloys is required to impart acceptable oxidation resistance.
- concentration of the reactive element greatly exceeds that of the impurities with which it reacts, the formation of extraneous, low melting point phases can result. If the proportion of the reactive element is too high or too low, the oxidation characteristics of the alloy may be suboptimal.
- the inventors have discovered that by the addition of aluminum to the nickel-chromium base alloy, oxidation resistance is enhanced by the formation of an impervious layer of aluminum oxide. To ensure that the surface oxide layer remains intact with a "self-healing" mechanism if the oxide is damaged or spalls, it is necessary to have aluminum dissolved uniformly in the alloy matrix to a level of about 3-6%, and preferably about 4% by weight. At this level, it is thought that diffusion of the aluminum atoms in the matrix can occur quickly to replace aluminum depletion by alumina formation at the surface.
- the limited solubility of aluminum in the nickel-chromium alloy can result in precipitation of some of the aluminum in the form of a nickel-aluminum phase referred to as "gamma prime. " As noted earlier, these particles can cause severe hardening in the alloy and a reduction in the aluminum in solution in the surrounding matrix.
- the inventors have developed the disclosed alloy so that it may serve as a thermocouple sheath, tube, wire, or strip for use as a heating element or as a tubular member in applications which are exposed to an oxidizing atmosphere at high temperatures.
- the disclosed alloys provide for favorable oxidation resistance at the highest temperatures of intended use without spalling of the surface oxide.
- Yttrium, calcium, and zirconium in the proper relative amounts effectively reduce the oxygen and sulfur content of the resulting alloy.
- these highly reactive additions are present uniformly in the matrix of the alloy. This ensures initial reaction of aluminum in the matrix at the hot surface with the ambient air/atmosphere and provides a base for bonding subsequent layers of aluminum oxide.
- the control of sulfur in the alloy by calcium and yttrium tends to neutralize the potential of this undesirable impurity to interfere with oxide layer formation.
- the chemistry of the alloys disclosed requires refining the melt to neutralize the sulfur and oxygen contained in the alloy. Hot fabricability is promoted through the addition of zirconium in the disclosed amounts and sequence during melting. The precipitation of "gamma prime" is retarded by increasing the solid solubility of aluminum in the nickel-chromium base alloy. As a result, cold working processes are facilitated.
- the disclosed alloys promote formation of a continuous protective layer of alumina.
- adherence of the oxide layer to the base alloy is ensured during thermal cycling, thereby promoting longer life at higher temperatures over comparable alloys which are presently available.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Microelectronics & Electronic Packaging (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Heat Treatment Of Articles (AREA)
- Investigating And Analyzing Materials By Characteristic Methods (AREA)
- Fuel Cell (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Materials For Medical Uses (AREA)
- Soft Magnetic Materials (AREA)
- Resistance Heating (AREA)
Abstract
Description
Claims
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US138484 | 1998-08-24 | ||
US09/138,484 US6093369A (en) | 1994-04-08 | 1998-08-24 | Modified nickel-chromium-aluminum-iron alloy |
PCT/US1999/018187 WO2000011230A1 (en) | 1998-08-24 | 1999-08-11 | Modified nickel-chromium-aluminum-iron alloy |
Publications (3)
Publication Number | Publication Date |
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EP1114197A1 EP1114197A1 (en) | 2001-07-11 |
EP1114197A4 true EP1114197A4 (en) | 2002-08-14 |
EP1114197B1 EP1114197B1 (en) | 2005-01-19 |
Family
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Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP99945036A Expired - Lifetime EP1114197B1 (en) | 1998-08-24 | 1999-08-11 | Modified nickel-chromium-aluminum-iron alloy |
Country Status (9)
Country | Link |
---|---|
US (1) | US6093369A (en) |
EP (1) | EP1114197B1 (en) |
JP (1) | JP2002523620A (en) |
AT (1) | ATE287457T1 (en) |
AU (1) | AU5773399A (en) |
CA (1) | CA2341660C (en) |
DE (1) | DE69923330T2 (en) |
MX (1) | MXPA01001953A (en) |
WO (1) | WO2000011230A1 (en) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
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US7451966B1 (en) * | 2001-07-02 | 2008-11-18 | Knowles Gareth J | Isolator mount for shock and vibration |
US7019269B2 (en) * | 2001-08-13 | 2006-03-28 | Sanyo Netsukogyo Kabushiki Kaisha | Heater |
EP1568977A1 (en) * | 2004-02-26 | 2005-08-31 | Borealis A/S | Shield for use in dehydrogenation reactors |
DE102009022714B4 (en) | 2008-05-27 | 2014-01-02 | Alstom Technology Ltd. | Method for oxidizing a thermocouple protective tube |
JP5819651B2 (en) * | 2010-07-21 | 2015-11-24 | 日本特殊陶業株式会社 | Glow plug |
CN105132751B (en) * | 2015-09-14 | 2017-08-22 | 四川六合锻造股份有限公司 | A kind of Ni Cr Al Fe systems high-temperature alloy material, its preparation method and application |
CN108754237A (en) * | 2018-05-15 | 2018-11-06 | 昆明理工大学 | A kind of method for preparing powder metallurgy of Ni-Cr-Al-Fe systems high temperature alloy |
JP7469072B2 (en) * | 2020-02-28 | 2024-04-16 | 株式会社神戸製鋼所 | Aluminum alloy forgings and their manufacturing method |
CN115074581A (en) * | 2022-06-27 | 2022-09-20 | 兰州理工大学 | Nickel-chromium-aluminum-silicon electrothermal alloy |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1995027803A1 (en) * | 1994-04-08 | 1995-10-19 | Hoskins Manufacturing Company | Modified nickel-chromium-iron-aluminium alloy |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2515185A (en) * | 1943-02-25 | 1950-07-18 | Int Nickel Co | Age hardenable nickel alloy |
US4460542A (en) * | 1982-05-24 | 1984-07-17 | Cabot Corporation | Iron-bearing nickel-chromium-aluminum-yttrium alloy |
JPS5985836A (en) * | 1982-11-10 | 1984-05-17 | Toshiba Corp | Hard alloy |
US4671931A (en) * | 1984-05-11 | 1987-06-09 | Herchenroeder Robert B | Nickel-chromium-iron-aluminum alloy |
-
1998
- 1998-08-24 US US09/138,484 patent/US6093369A/en not_active Expired - Lifetime
-
1999
- 1999-08-11 DE DE69923330T patent/DE69923330T2/en not_active Expired - Lifetime
- 1999-08-11 WO PCT/US1999/018187 patent/WO2000011230A1/en active IP Right Grant
- 1999-08-11 AT AT99945036T patent/ATE287457T1/en not_active IP Right Cessation
- 1999-08-11 JP JP2000566480A patent/JP2002523620A/en active Pending
- 1999-08-11 MX MXPA01001953A patent/MXPA01001953A/en unknown
- 1999-08-11 AU AU57733/99A patent/AU5773399A/en not_active Abandoned
- 1999-08-11 CA CA2341660A patent/CA2341660C/en not_active Expired - Lifetime
- 1999-08-11 EP EP99945036A patent/EP1114197B1/en not_active Expired - Lifetime
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1995027803A1 (en) * | 1994-04-08 | 1995-10-19 | Hoskins Manufacturing Company | Modified nickel-chromium-iron-aluminium alloy |
Non-Patent Citations (1)
Title |
---|
SIKKA V K: "MICROSTRUCTURAL EVALUATION OF NICKEL-BASED SAMPLES FROM HOSKINS MANUFACTURING COMPANY", MICROSTRUCTURAL EVALUATION OF NICKEL-BASED SAMPLES FROM HOSKINS MANUFACTURING COMPANY, XX, XX, PAGE(S) COMPLETE, XP002922474 * |
Also Published As
Publication number | Publication date |
---|---|
WO2000011230A1 (en) | 2000-03-02 |
EP1114197A1 (en) | 2001-07-11 |
US6093369A (en) | 2000-07-25 |
ATE287457T1 (en) | 2005-02-15 |
CA2341660C (en) | 2014-05-13 |
DE69923330D1 (en) | 2005-02-24 |
CA2341660A1 (en) | 2000-03-02 |
EP1114197B1 (en) | 2005-01-19 |
AU5773399A (en) | 2000-03-14 |
MXPA01001953A (en) | 2002-04-24 |
DE69923330T2 (en) | 2006-05-18 |
JP2002523620A (en) | 2002-07-30 |
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